Polyesters blended with cyclic ester polymers

ABSTRACT

Uniform, thermoplastic, normally solid blends containing cyclic ester polymers and thermoplastic, normally solid polymer which can be a condensation polymer, and/or an addition polymer of olefinically unsaturated monomers having no more than one hydrogen bonded to each carbon of each olefinically unsaturated group thereof, including such polymers as cellulose derivatives, nylons, polyester polymers, polyoxyalkylenes, polycarbonates, poly(fluorocarbons), coumarone-indene resins, maleic acid or anhydride addition polymers and copolymers, stilbene addition polymers and copolymers, chlorinated polyethers, aromatic poly(hydroxy ether) polymers, polysufones, polypeptides, etc. These novel blends are useful in the production of fibers, films, coatings, adhesives, wire and cable coatings, molding materials, extrusion materials, or shaped articles, having one or more unique properties, such as, dyeability, improved stress crack resistance, improved optical properties, e.g., improved hiding power, low haze, high gloss and/or high light transmission, improved plasticization, improved toughness, improved melt processability, improved impact resistance, and/or improved ability to disperse additives, such as, fillers coloring agents, antioxidants, extenders, etc.

United States Patent [191 Koleske et al.

[ POLYESTERS BLENDED WITH CYCLIC ESTER POLYMERS [75] Inventors: Joseph Victor Koleske; Clyde Jesse Whitworth, Jr., both of Charlestown, W. Va.; Robert Dean Lundberg, Somerville, NJ.

[73] Assignee: Union Carbide Corporation, New

York, NY.

[22] Filed: Oct. 11, 1973 [21] Appl. No.: 405,525

Related US. Application Data [60] Division of Ser. No. 140,951, May 6, 1971, Pat. No. 3,781,381, which is a continuation-in-part of Ser. No, 812,314, April 1, 1969, abandoned.

[56] References Cited UNITED STATES PATENTS 3,312,753 4/1967 Bailey, Jr. 260/860 3,331,890 7/1967 Caldwell et a1. 260/75 3,502,623 3/1970 Hurworth et a1. 260/860 Primary ExaminerMelvin Goldstein Assistant Examiner-T. Pertilla Attorney, Agent, or Firm-F. M. Fazio [451 July 1, 1975 [5 7] ABSTRACT Uniform, thermoplastic, normally solid blends containing cyclic ester polymers and thermoplastic, normally solid polymer which can be a condensation polymer, and/or an addition polymer of olefinically unsaturated monomers having no more than one hydrogen bonded to each carbon of each olefinically unsaturated group thereof, including such polymers as cellulose derivatives, nylons, polyester polymers, p0- lyoxyalkylenes, polycarbonates, poly(fluorocarbons), coumarone-indene resins, maleic acid or anhydride addition polymers and copolymers, stilbene addition polymers and copolymers, chlorinated polyethers, aromatic poly(hydroxy ether) polymers, polysufones, polypeptides, etc

These novel blends are useful in the production of fibers, films, coatings, adhesives, wire and cable coatings, molding materials, extrusion materials, or shaped articles, having one or more unique properties, such as, dyeability, improved stress crack resistance, improved optical properties, e.g., improved hiding power, low haze, high gloss and/or high light transmission, improved plasticization, improved toughness, improved melt processability, improved impact resistance, and/or improved ability to disperse additives, such as, fillers coloring agents, antioxidants, extenders, etc.

8 Claims, No Drawings POLYESTERS BLENDED WITH CYCLlC ESTER POLYMERS This application is a division of application Ser. No. 140,951, filed May 6, 1971, now US. Pat. No. 3,781,381, issued Dec. 25, 1973 which in turn is a continuation-in-part of application Ser. No. 812,314, now abandoned, entitled Uniform, Thermoplastic, Normally Solid Compositions Containing Diverse Components", by .l. V. Koleske, C. J. Whitworth, Jr., and R. D. Lundberg, filed Apr. 1, 1969, all of the aforesaid applications being assigned to a common assignee.

BACKGROUND OF THE INVENTION a. Field of the Invention The present invention relates to novel uniform, thermoplastic, normally solid polymer blends containing normally solid, thermoplastic polymers, such as, condensation polymers and addition polymers of olefinically unsaturated monomers having no more than one hydrogen bonded to each carbon of each olefinically unsaturated group thereof, in intimate association with cyclic ester polymers, such as polymer of epsiloncaprolactone, and having a wide range of application in the production of fibers, films, and other shaped articles. As used herein, the term polymer includes homopolymers, copolymers, terpolymers, etc., and, in general, a polymer made by polymerizing any number of monomers.

b. Description of the Prior Art Thermoplastic polymers in the nature of normally solid condensation polymers and addition polymers of the type described herein including cellulose derivatives, nylons or polyamides, polypeptides, polyoxyalkylenes, polycarbonates, polyurethanes, polysulfones, poly(hydroxy ether) polymers, polyimides, polyureas, polyester polymers, maleic anhydride copolymers, stilbene homopolymers and copolymers, and the like have been long known and extensively used in the manufacture of household articles, industrial and commercial articles, wearing apparel, adhesives, molding compositions, extrusion compositions, protective coatings, wire and cable coatings, conduits hoses and a wide variety of other articles. While such heretofore known thermoplastic, normally solid polymers possess important and unique properties which enhance their widespread use for a great many applications, there has been a need to modify or correct certain undesirable properties in order to widen the field of use of such materials or to improve their current field of application.

For example, many of these thermoplastic polymers would be chosen for a particular use on the basis of their peculiar properties, except that they may be too stiff and difficult to shape and form or they may need improvement in other areas such as stress crack resistance, impact resistance, or optical properties. Another area of potential improvements by modification is in the melt processibility of the thermoplastic polymers, especially when using additives, such as, fillers, pigments, dye stuffs, anti-oxidants, stabilizers and other to be blended into the polymers. Due to the highly viscose and sticky nature of the thermoplastic polymers during processing, it is sometimes extremely difficult to disperse the additives uniformly throughout the polymer.

Attempts to prepare useful polymeric blends of two or more polymers have generally been unsuccessful. Blends of different types of polymers are often incompatible, and this incompatibility usually results in a marked deterioration or loss of the physical properties characteristic of each of the unblended polymers. Even where the two polymers are compatible in the melt, they often tend to separate into segregated domains of each individual polymer species. This segregation into separate domains results in a non-uniform mass and usually results in a marked deterioration of the physical properties which would be characteristic of either of the unblended polymers or copolymers.

Because of these factors, a large technology of copolymers has developed employing comonomers with varying degrees of success. By proper choice of such comonomers, copolymerization of different chemical units within the same polymer chain can be achieved to give some desirable properties in certain specific instances. Physical mixing or blending of the modifier, because of its simplicity and ease of performance. is preferred over the chemical or copolymerizing technique but has not been heretofore achievable over a wide range of the diverse thermoplastic polymers known and described herein. This invention now permits the blending of a wide range of diverse thermoplastic, normally solid polymers with cyclic ester polymers to form uniform polymer blends having useful and desirable properties over a broad composition range. It is believed that the presence of the cyclic ester polymer lessens segregation of the two polymers into separate domains and prevents the significant loss of physical properties which would be associated with such segregation.

Usually when one mixes or blends polymers, incompatibility is the expected result and compatibility of the polymers is not expected unless very small amounts of one of the components are added or if the polymers are very similar in nature as, for example, high and low density polyethylene. However, in certain instances blends of polymers can have commercial utility but in most cases the blended polymers had to be similar in nature or present in very small amounts to be compatible and no one polymer was blended with a wide range of diverse polymers with the possible exception of nitrocellulose. As summaried in Principles of Polymer Chemistry, Paul J. Flory, Cornell University Press, Ithaca, New York, 1953, at page 555 incompatibility of chemically dissimilar polymers is observed to be the rule and compatibility is the exception.

SUMMARY OF THE INVENTION The present invention provides novel uniform, thermoplastic polymeric blends and provides a means for readily altering the properties of such important plastics as thermoplastic, normally solid condensation polymers including polyoxyalkylenes, polycarbonates, cellulose esters, cellulose ethers, polyurethanes, polysulfones, polyamides, e.g., nylons, poly(hydroxy ethers), polyimides, polyureas, polyester polymers, and addition polymers of olefinically unsaturated monomers having no more than one hydrogen on each carbon of each olefinically unsaturated group thereof, to impart highly desirable properties not easily obtained in such plastics prior to this invention.

Heretofore, it was the case that, in many instances, when a polymeric modifier was attempted to be added to thermoplastic polymers of these types, the polymers would not accept the polymeric modifier and there resulted non-uniform masses and nonuniform, deteriorated properties.

This is not the case with the novel thermoplastic, norally solid compositions of this invention which conan cyclic ester polymers uniformly blended through- .t with a thermoplastic, normally solid polymer. Un- .e the previous attempts to form uniform blends of ch thermoplastics with substantial amounts of poly- :ric modifiers, the thermoplastic polymers readily acpt the cyclic ester polymer blended therein through a present invention. This ease of acceptance of cyclic ter polymers is surprising in that it applies throughout diverse range of thermoplastic polymers to provide verse improvements in the properties of the thermoastic polymer. Despite the presence of cyclic ester 'lymer uniformly blended in the thermoplastic polyar, its beneficial properties are not greatly affected. When the cyclic ester polymer is added and blended th the thermoplastic polymer, the processability of e thermoplastic polymer is considerably improved. at only are the milling characteristics of the thermoastic enhanced, but also additives, such as fillers, aclerators, coloring agents, and other common plastic ,ditives are more readily dispersed throughout the ass of the thermoplastic.

The handling and shaping of the novel thermoplastic, rmally solid compositions to fabricate shaped arties are also facilitated. The novel compositions are are readily spread to conform to the configuration of olds and can be formed into sheets or other shapes rich are easier to handle and fabricate in the desired anner in the soft or molten state. The novel composims possess other advantages which will appear hereafter on a case by case basis.

The cyclic ester polymers which are contemplated in e practice of the invention are those which possess a duced viscosity of at least about 0.1, and desirably am about 0.2 to about 15, and higher. The preferred lymers of cyclic esters for many applications have a duced viscosity value of from about 0.3 to about 5. iese polymers are further characterized by the folwing recurring structural linear Unit I:

tried ierein each R, individually, is selected from the class nsisting of hydrogen, alkyl, halo and alkoxy; A is the ;y group; x is an integer from 1 to 4; y is an integer )m 1 to 4; z is an integer of zero or one; with the pro- ;os that (a) the sum of x y z is at least 4 and not eater than 7, and (b) the total number of R variables rich are substituents other than hydrogen does not ceed 3, preferably does not exceed 2, per unit. Illusitive R variables include methyl, ethyl, isopropyl, nltyl, sec-butyl, t-butyl, hexyl, chloro, bromo, iodo, ethoxy, ethoxy, n-butoxy, n-hexoxy, 2-ethylhexoxy, decoxy, and the like. It is preferred that each R, indidually, be hydrogen, lower alkyl, e.g., methyl, ethyl, propyl, isobutyl, and/or lower alkoxy, e.g., methoxy, boxy, propoxy, n-butoxy, and the like. It is further eferred that the total number of carbon atoms in the substituents does not exceed 20.

In one embodiment, highly desirable cyclic ester rlymers which are contemplated are characterized by both recurring structural Unit 1 supra and recurring structural Unit II:

T, oc-- wherein each R is selected from the class consisting of, individually, hydrogen, alkyl, cycloalkyl, aryl, and chloroalkyl, and, together with the ethylene moiety of the oxyethylene chain of Unit II, a saturated cycloaliphatic hydrocarbon ring having from 4 to 8 carbon atoms, desirably from 5 to 6 carbon atoms. It is preferred that recurring Unit II contains from 2 to 12 carbon atoms. Illustrative R variables include methyl, ethyl, n-propyl, isopropyl, t-butyl, the hexyls, the dodecyls, 2 -chloroethyl phenyl, phenethyl, ethylphenyl, cyclopentyl, cyclohexyl, cycloheptyl, and the like. It is preferred that R" be hydrogen; lower alkyl, e.g., methyl, ethyl, npropyl, isopropyl; chloroalkyl, e.g., 2 -chloroethyl; and the like.

The aforedescribed recurring linear unit (I) is interconnected through the oxy group (O-) of one unit with the carbonyl group of a second unit. In different language, the interconnection of these units does not involve the direct bonding of two carbonyl groups, i.e.,

With relation to the relatively high molecular weight cyclic ester polymers, the terminal moieties thereof are not determinable by infrared analysis which factor is readily understandable since macromolecules are involved. On the other hand, the relatively lower molecu lar weight cyclic ester polymers, e.g., those having reduced viscosity values below about 0.25 are characterized by end groups which can be hydroxyl; carboxyl; hydrocarbyl, such as, alkyl, cycloalkyl, aryl, aralkyl, and alkaryl; hydrocarbyloxy, such as, alkoxy, cycloalkoxy; aryloxy, aralkoxy, and alkaryloxy; and possibly other moieties such as catalyst residue; and mixtures of the foregoing. It may be desirable in certain instances that the hydroxyl and carboxyl end groups, if present, be esterified or acylated to render them inert such as by reacting the hydroxyl moiety with a monocarboxyl compound or its corresponding anhydride, e.g., acetic acid, acetic anhydride, butyric acid 2-ethylhexanoic acid, benzoic acid, etc., or by reacting the carboxyl moiety with a monohydroxyl compound such as a monohydric alcohol or monohydric phenol, e.g., methanol, 2-ethylhexanol, isobutanol, phenol and the like.

When the cyclic ester polymers are prepared from a mixture containing the cyclic ester monomer and a cyclic ether which is copolymerizable therewith, e.g., alkylene oxide, oxetane, tetrahydrofuran, etc., the polymeric chain of the resulting copolymeric product will be characterized by both recurring linear Unit I supra as well as the recurring linear Unit II which would represent the alkylene oxide comonomer polymerized therewith. When the comonomer is an alkylene oxide, then the resulting copolymeric product will contain both recurring linear Unit I and recurring linear Unit ll in the copolymeric chain thereof. The interconnection of linear Unit land linear Unit I] supra does not involve or result in the direct bonding of two oxy groups, i.e., -OO--. In other words, the oxy group -O) of recurring linear Unit ll is interconnected with the carbonyl group of recurring linear Unit supra or with the alkylene moiety of a second oxyalkylene Unit (ll).

Particularly preferred polymers of cyclic esters are those which are characterized by the oxypentamethylenecarbonyl chain as seen in recurring structural Unit Ill:

o c C wherein each R, is hydrogen or lower alkyl, preferably hydrogen or methyl, with the proviso that no more than three R, variables are substituents other than hydrogen.

The preparation of the cyclic ester polymers is well documented in the patent literature as exemplified by US. Pat. Nos. 3,021,309 through 3,021,317; 3,l69,945; and 2,962,524, and Canadian Pat. No. 742,294. Briefly, the process involves the polymerization of an admixture containing at least one cyclic ester monomer with or without a functional (e.g., active hydrogemcontaining) initiator therefor, and a suitable catalyst, the choice of which will depend on the presence or absence of added initiator.

Suitable monomeric cyclic esters which can be employed in the manufacture of the cyclic ester polymers are best illustrated by the following formula:

(lll) wherein the R, A, x, y, and z variables have the significance noted in Unit l supra.

'Representative monomeric cyclic esters which are contemplated include, for example, deltavalerolactone; epsiloncaprolactone; zetaenantholactone; eta-caprylolactone; the monoalkyldelta-valerolactones, e.g., the monomethyl-, monoethyl-, monohexyl-, delta-valerolactones, and the like; the dialkyl-delta-valerolactones, e.g., the dimethyl-, diethyl-, and di-n-octyl-delta-valerolactones, and the like; the monoalkyl-, Y dialkyl-, and trialkyl-epsiloncaprolactones, e.g., the monomethyl-, monoethyl-, monohexyl-, dimethyl-, diethyl-, di-n-propyl-, di-nhexyl-, trimethyl-, triethyl-, and tri-n-propyl-epsilon- 6 caprolactones, and the like; the monoalkoxy-and dialkoxy-delta-valerolactones and epsiloncaprolactones, e.g., the monoethoxy-, monoisopropoxy-, dimethoxy-, and diethoxy-deltavalerolactones and epsilon-caprolactones, and the like; I ,4-dioXane-2-one; dimethyll ,4-dioxane-2-one, and the like. A single cyclic ester monomer or mixtures of such monomers may be employed.

In the absence of added functional initiator, the polymerization process is desirably effected under the operative conditions and in the presence of anionic catalysts as noted in U.S. Pat. Nos. 3,021,309 to 3,021.3 l 7, such as, dialkylzinc, dialkylmagnesium, dialkylcamdium, trialkylaluminum, dialkylaluminum alkoxide, alkylalumi num dialkoxide, dialkylaluminum halide, aluminum trialkoxide, alkyllithium, and aryllithium. Specific anionic catalystswould include di-n-butylzinc, diethylmagnesium, di-n-butylmagnesium, dimethylcadmium, diethylcadmium, di-t-butylcadmium, triethylaluminum, triisobutylaluminum, tri-Z-ethylhexylaluminum, aluminum triisopropoxide, aluminum triethoxide, ethyllithiium, n-butyllithium, phenyllithium, and the like.

When employing an admixture containing cyclic ester monomer and functional initiator which possesses at least one active hydrogen substituent, e.g., amino, carboxyl, and hydroxyl, it is desirable to use the catalysts noted in US. Pat. Nos. 2,878,236, 2,890,208, 3,169,945, and 3,284,417 under the operative conditions discussed therein. In these processes the active hydrogen substituent on the initiator is capable of opening the monomer cyclic ester ring whereby said cyclic ester is added to said initiator as a substantially linear group thereto. The molecular weight of the resulting polymers of cyclic ester can be predetermined by controlling the molar ratios of cyclic ester monomer to be added to the functional initiator. Amino and hydroxyl substituents on the initiator will result in polymeric products having hydroxyl end group. Carboxyl substituents on the initiator will result in polymeric products having Carboxyl end-group. The initiator with the active hydrogen atom will thus be contained in the final polymeric molecule. The esterification or acylation of the afore-mentioned end-groups has been described previously and is voluminously documented in the art.

Polymers of cyclic esters can also be manufactured via the process described in US. Pat. No. 2,962,524. In this process, a monomeric admixture comprising cyclic ester and alkylene oxide which desirably has the forwherein each R, individually, has the meanings noted in Unit ll supra, can be reacted with a monofunctional and/or polyfunctional (e.g., active hydrogencontaining) initiator possessing amino, hydroxyl, and- /or carboxyl groups, preferably in the presence of a Lewis acid catalyst such as boron trifluoride. Illustrative alkylene oxides would include ethylene oxide, propylene oxide, the butylene oxides, styrene oxide, epichlorohydrin, cyclohexene oxide and the like.

Cyclic ester/alkylene oxide copolymers can also be repared by reacting in the absence of an active hydroen-containing initiator an admixture comprising cyclic ster and .alkylene oxide monomers, an interfacial gent such as a solid, relatively high molecular weight oly(vinyl stearate) or lauryl methacrylate/vinyl chlode copolymer (reduced viscosity in cyclohexanone at C. of from about 0.3 to about 1.0), in the presence f an inert normally-liquid saturated aliphatic hydroarbon vehicle such as heptane, phosphorus pentafluode as the catalyst therefor, at an elevated temperalre, e.g., about 80C. and for a periodof time suffiient to produce such cyclic ester/alkylene oxide coolymers.

The cyclic ester polymers employed herein contain in re polymeric chain at least a major molar amount, i.e., reater than about 50, preferably about 80, to about 00 mol percent of Units I and up to a minor molar mount, i.e., about 0 to less than about 50, preferably p to about 20, mol percent of other units such as alkylne oxide Units II, initiator residues or moieties, catast residues, and other difunctional and/or monofunconal units. The cyclic ester polymers containing about 00 mol percent of Unit I are preferred and those' in 'hich Unit I represents the oxypentamethylene caronyl moiety are most preferred. In various desirable mbodiments there can be employed cyclic ester polyiers which contain from 100 to about mol percent f Units I supra and from 0 to about 90 mol percent of [nits II supra in the polymeric chains thereof.

As mentioned previously, the polymers of cyclic es- :rs which are contemplated are expressed in terms of ieir reduced viscosity values. As is well known in the rt, reduced viscosity value is a measure or indication f the molecular weight of polymers. The expression reduced viscosity" is a value obtained by dividing the pecific viscosity by the concentration of polymer in 1e solution, the concentration being measured in rams of polymer per l00 milliliters of solvent. The pecific viscosity is obtained by dividing the difference etween the viscosity of the solution and the viscosity f the solvent by the viscosity of the solvent. Unless therwise noted, the reduced viscosity values herein eferred to are measured at a concentration of 0.2 gram f polymer in 100 milliliters of benzene (benzene is referred although cyclohexanone, chloroform, tolune or other organic solvent for the polymer may be sed) at 30C.

Mixtures of homopolymers and/or copolyrn'ers, terolymers etc. made from different cyclic esters can be mployed in this invention.

The cyclic ester polymer can be fluxed on a mill and heeted off to form sheets or films. It can be extruded s a tape, rope, or other shape or can be extruded and elletized. When formed by the dispersion polymerizalon technique, the cyclic ester polymer is obtained in owder or granular form. It can also be dissolved in a uitable solvent, such as, benzene, toluene, 4 2- itropropane, methylene chloride and other solvents.

dethylene chloride and other fast drying solvents may e preferred when the cyclic ester is used as a solution. \lthough the cyclic ester polymer can be used in this ivention in any of the above-mentioned forms it is ,sually preferred to use it in the form of powders, gran-. .les or pellets.

The thermoplastic organic polymer component of be novel blends disclosed and claimed herein are well known to those skilled in the 'plastics art. For the purposes of this invention the thermoplastic polymers are classified into two categories; nanielygthermoplastic condensation polymers other than the cyclic ester a mers ,disclosed hereinfand thermoplastic additio'n'polymers, including copolymer's,.terpolymers, etc.', of polymerizable olefinically unsaturated monomers having not more than one hydrogen bonded'toeach carbon ofeach olefinically unsaturated group thereof.-

The term condensation polymers as used herein is consistent with the polymer classification set forth in Principles of Polymer Chemistry by Paul J. Flory, 'Cor' nell University Press, Ithaca, New York, 1953, at pages 37-50 and 57-61, and particularly in the paragraph bridging pages 39 and 40 and the one bridging pages 57 and 59. Thus, the term is not liri ited to those polymers which are produced with concurrent evolution of low molecular weight substances, such as, water, 'HCl NaCl and the like, but also include polymers produced by polymerization with no evolution of low molecular weight by-products and which contain interunit linkages not found in the monomers, e.g., the polyurethanes, polyureas, and the like, and to polymers produced by the addition polymerization of cyclic monomers, e.g., polyoxyalkylenes, chlorinated polyoxyalkylenes, polyimides, polylactams and the like. Suitable condensation polymers also include derivatives, i.e., the ethers and esters, of cellulose which is consistent withqFlorys classification (pages 40 and 43). The condensation polymers employed herein are thermoplastic and normally solid, i.e., solid at ambient temperatures.

Typical thermoplastic condensation polymers include the thermoplastic poly(hydroxy ether) polymers preferably the thermoplastic aromatic poly(hydroxy ether) polymers formed by the condensation of aliphatic and aromatic polyhydroxy compounds, e.g., alcohols, carboxylic acids and phenols,'preferably aromatic dihydroxy compounds or phenols having 6 to 24 carbon atoms with an epihalohydrin. An illustration is the polycondnsate of bisphenol A and epichlorhydrin to form a thermoplastic polymer having recurring groups of the formula;

Another class of thermoplastic condensation polymers suitable for use herein is the polycarbonate class,

preferably aromatic polycarbonates derived from aro matic dihydroxy compounds or'phenols having 6' to'24 carbon atoms and phosgene. An illustration istl'ie polycarbonate made by reacting phosgene' with bisphenol A and having the recurring unit q oco Another class of thermoplastic condensation polymers is the polysulfones, preferably the aromatic polysulfones derived from aromatic dihydroxy compounds having 6 to 24 carbon atoms and di(chloroaryl) sulfones. An illustration is the polysulfone made by reacting bisphenol A and di(parachlorophenyl) sulfone and having the recurring unit of the formula:

CH3 F The thermoplastic cellulosic esters and ethers are widely used as molding, coating and film-forming materials and are well known. These thermoplastic condensation polymers can also be used as the thermoplastic component in the practice of this invention. These materials include the solid thermoplastic forms of cellulose nitrate, cellulose acetates, (e.g., cellulose diacetate, cellulose triacetate), cellulose butyrate, cellulose acetate butyrate, cellulose propionate, cellulose tridecanoate, carboxymethyl cellulose, ethyl cellulose, hydroxyethyl cellulose and acetylated hydroxyethyl cellulose as described on pages 165-170 of Modern Plastics Encyclopedia, 1962, and references listed therein.

Another class of thermoplastic condensation poly mers is the polyamides, such as, nylon 6 (e.g., polycaprolactam), nylon 6/6 (e.g., hexamethylenediamineadipic acid or anhydride polycondensate), nylon 6/10 (e.g., hexamethylenediamine-sebacic or anhydride polycondensate), nylon 8 (e.g., N-alkoxymethylhexamethylenediamine-adipic acid or anhydride polycondensate), nylon 11 (e.g. ll-aminoundecanoic acid polycondensate) and the like as described on pages 219-227 of Modern Plastics Encyclopedia, 1962, and references listed therein. Suitable for use herein are polyamides of hydrocarbon dicarboxylic acids having 2 to 18 carbon atoms and hydrocarbon diamines having 2 to 18 carbon atoms and homopolymers of such diamines.

Another class of thermoplastic condensation polymers is the normally solid thermoplastic polyoxyalkylene polymers, both unsubstituted and halogenated. The lowest homologous type of this class is the polyoxymethylene polymers, otherwise called acetal resins, and are described on pages 140-142 of Modern Plastics Encyclopedia, 1962. In addition, the normally solid polyoxyethylcne, polyoxypropylene, and polyoxybutylene polymers and copolymeric forms, e.g., poly(oxyethyleneoxypropylene) copolymers wherein the oxyethylene units are randomly distributed or present in blocks, poly(oxymethyleneoxyethylene) copolymers and poly(oxymethyleneoxypropylene) copolymers having a block or random distribution are all well known and can be employed as the thermoplastic component. The halogenated polyoxyalkylene normally solid polymers are also well known and are suitable for use in the novel blends of this invention. For example,

the chlorinated polyethers made and sold under the name of Penton by Hercules Powder Company (pages 171-172 Modern Plastics Encyclopedia. 1962) and having the recurring unit of the formula:

CH Cl CH2 cn o CH Cl can be used. The chlorinated polyethers made and sold under the name Hydrin by B. F. Goodrich Company and having the recurring unit of the formula:

EH 6 CH HO as well as copolymers containing such units and oxyethylene units, Cl-l CH O--, in random or block distribution, also are suitable as the thermoplastic component. These are made by addition polymerization of epichlorhydrin which can be conducted with ethylene oxide if the copolymer is desired. Other oxyalkylene units can be provided in place of or in addition to oxyethylene by the addition polymerization of other alkylene oxides with chlorinated oxetane (used to produce Penton) or epichlorhydrin.

Another class of thermoplastic condensation polymers is the normally solid polyester polymers of polyhydric, preferably dihydric, alcohols having 2 to 18 carbon atoms and polycarboxylic, preferably dicarboxylic, acids or acid anhydrides having 2 to 18 carbon atoms, for example, those described in pages 244-250, Modern Plastics Encyclopedia, 1962, and references cited therein. Examples of suitable polyester polymers are poly(ethylene terephthalate), poly(l,3-propylene maleate), poly(ethylene fumarate), poly(diethylene phthalate), poly(2,3-butylene adipate), and the like.

Polyurethanes, otherwise known as isocyanate resins, also can be modified in accordance with this invention. Some of these thermoplastic condensation polymers are described on pages 216-218 of Modern Plastics Encyclopedia, 1962, and references cited therein. For example, polyurethanes formed from toluene diisocyanate (TDI) or diphenyl methane 4,4-diisocyanate (MDI) and a wide range of polyols, such as, polyoxyethylene glycol, polyoxypropylene glycol, hydroxyterminated polyesters, polyoxyethylene-oxypropylene glycols are suitable. The thermoplastic, normally solid polyurethanes described in Saunders & Frisch, Polyurethanes: Chemistry And Technology", lnterscience Publishers, New York, Part I, Chemistry, published in 1963 and Part 11, Technology", published in 1964 can be used.

The polyureas can also be advantageously modified by cyclic ester polymers according to this invention.

1 1 iitable polyureas are thermoplastic solids having reirring units of the formula: {[NHRNH- lCh carbon atom of each olefinically unsaturated oup thereof, i.e., monomers having the group, C=C each carbon of which is bonded to O or 1 hyogen atom but not 2. Monomers of this type include aleic acid or acid anhydride, fumaric acid, stilbene, 'clohexene, cyclobutene, tetrafluoroethylene, hexaioropropylene, trifluoroethylene, chlorotrifluoethylene, tetrahydrophthalic acid or acid anhyides, 3,4-dimethyl-2-pentene, terpene, 2-hexene, 3- :ptene, coumarone, indene and the like. Thermoplasnormally solid homopolymers or copolymers of one more monomers of the type listed above are suitable, g., the fluorocarbon polymers, namely, poly(tetraioroethylene), poly(trifluoroethylene), poly(chlorofluoroethylene), and poly(hexafluoropropylene) deribed in pages 198-202, Modern Plastics Encyclopea, 1962, and references cited; the coumarone-indene sins, petroleum resins and polyterpene resins deribed in pages 174-1 75 and cited references of Modn Plastics Encyclopedia, I962; maleic acid or acid an- 'dride addition polymers and copolymers, e.g., maleic lhydride-methyl vinyl ether, maleic anhydride-ethyl nyl ether and maleic anhydride-isobutyl vinyl ether ldition copolymers; stilbene addition polymers and polymers, e.g., stilbene-acrylonitrile copolymers, ld the like.

The relative proportions of cyclic ester polymer and ermoplastic, normally solid polymer employed in the ivel compositions of this invention can be varied over ry wide percentage ranges depending upon the par- :ular characteristics desired in the particular compoion being prepared and its intended use. For exame, the cyclic ester polymer can be present in amounts nging from about I to about 95% and the thermoplaspolymer component can be present in amounts nging from about 5 to about 99%, based on the total right of cyclic ester polymer and thermoplastic polyar component. It is preferred in most cases to utilize ninor amount of the cyclic ester polymer and a major mum of the thermoplastic polymer component. ore preferably, about 2 to about 40% of the cyclic ter polymer and about 60 to about 98% of the theraplastic polymer component are employed and most eferably about 5 to about 30% of the cyclic ester 'lymer and about 70 to about 95% of the thermoplaspolymer component are employed.

A surprising aspect of the present invention is the dis very that improved properties are obtained when en very small amounts of the cyclic ester polymer are ed. It is equally, if not more, surprising to have found at even major amounts of cyclic ester polymer, i.e.,

i to about 95 weight percent, do not completely oblitate the characteristic properties of the thermoplastic mponent. It is an extremely important discovery of' sitions, there results, in many systems, an easily prossable thermoplastic composition which can be molded atelevated temperatures and under pressures, if desired, to form thermoplastic articles having physicalproper'tiesi very close to the physical properties of articles madef rom the thermoplastic component alone. The novel compositions containing minor amounts of cyclic ester polymer can be molded or extruded to form sheets, plaques, pellets, tapes or other articles which are non-blocking and can be stacked one upon the other without sticking together. Subsequently, they can be shaped by molding at elevated temperatures and pressures or by other means. Even relatively minor amounts such as 30% or less decrease the stiffness of most thermoplastic components and render them less sticky and more easily worked.

The thermoplastic polymer component and cyclic ester polymer can be mixed or blended by any desired technique. For example, they can be blended on a tworoll mill, Brabender mixer, or other equipment at low to moderate temperatures, for example, in the range of C. or higher, for example, up to as high as 180 to 250C. However, the lower temperatures are usually suitable and are economically preferred.

Suitable equipment for fluxing the thermoplastic component and cyclic ester polymer together include Banbury mixers, Brabender mixers, screw extruders, two-roll mills, or any-other mixing devices adapted to mix highly viscous or semi-solid materials at low to moderate or high temperatures. The time of blending or fluxing is not narrowly critical and a sufficient blending time to obtain a substantially uniform blend is usually satisfactory. Mixing of the cyclic ester polymer and the thermoplastic component in the heated or molten state is believed to be facilitated by the partial hydrocarbon nature of the cyclic ester polymer. Either there can be no phase separation, or the phase separation is such that there is no deleteriour change of physical properties in blending the two different polymeric materials together in accordance with this invention.

Illustrative times of blending are in the range of l and 2 minutes to 30 minutes or an hour. In the usual case, about 5 to 15 minutes is adequate. After adequate blending, the novel thermoplastic composition is cooled to ambient temperature and thereafter can be shaped and/or formed in any desired manner. If desired, other materials can be added during blending, for example, the usual ingredients used in the compound ing of thermoplastic polymers can be employed. Such added materials can include fillers, antioxidants, light stabilizers, heat stabilizers, plasticizers, etc.

The novel thermoplastic compositions of this invention have improved physical properties which are at least similar to the physical properties of the major component of the composition. A most striking aspect of the invention is that additions of cyclic ester polymers in amounts over a wide range are readily accepted by a wide range of diverse thermoplastic polymers and at the same time retain the essential characteristic of the thermoplastic polymer.

In a preferred embodiment, the invention relates to 'novel -shaped and molded articles, especially fibers, "yarns, woven cloth, carpets, etc., which are formed from nov el blends of normally solid, thermoplastic polyamidessuch as the nylons illustrated previously and the cyclic iesterjpolymers. Such novel shaped and molded articlesexhibit outstanding characteristics such as excellent resistance to soiling and apparent soiling, good anti-static and non-cling properties, significant dioxide), favorable optical properties especially under artificial lighting, brighter yarn, etc. This significant improvement in characteristics is obtained while maintaining a desirable combination of other mechanical and physical properties in the novel shaped article.

In this preferred embodiment, the novel blends or shaped articles comprise cyclic ester polymers which contain from 100 to about molperceritof Units l supra and from 0 to about 95 mol percent of Units ll supra in the polymeric chains thereof, desirably from about 70 to about mol percent of Units I and from about 30 to about 90 mol percent of Units II, and preferably from about 60 to about mol percent of Units 1 and from about 40 to about 85 mol percent of Units ll. Other moieties or groups can be interspersed in the polymeric chains of the cyclic esters such as the urethane group, a

the monoand polyaromatic rings including fused and bridged rings such as phenylene, biphenylene, naphthylene, phenylene-alkylene-phenylene, and ph'enylenealkylidene-phenylene; initiator moieties; catalyst residues; etc. Such groups, if present, represent a small mol percent of the cyclic ester polymer. Such novel blends or shaped articles can contain up to about 15 weight per cent, and higher, of cyclic ester polymer, based on the total weight of polyamide and cyclic ester polymer. A concentration of from about one to about 10 weight per cent (and preferably from about 2 to about 7 weight per cent) cyclic ester polymer in the novel blend is generally sufficient to obtain novel shaped or molded articles which exhibit the outstanding properties noted previously.

DESCRIPTION OF SPECIFIC EMBODIMENTS The following examples are presented. Unless otherwise specified, all percentages and parts are by weight, all temperatures are on the Centigrade scale, and all reduced viscosities are measured at a concentration of 0.2 gram of polymer in 100 milliliters of benzene at about 30C. Figures given for physical properties in the tables below are averages of test results on two or more samples of each material and, in some instances, such averages have been rounded off.

The testing for various physical properties was done on an lnstron tensile tester using specimens about A inch wide, 0.020 to 0.30 inch thick and about 1 inch in gauge length. Gauge length is the length of the specimen between the jaws of the testing apparatus. The secant molulus or stiffness was determined at a strain rate of 10% in inches per inch per minutes and the other tensile property at a strain rate of 100% in inches per inch per minute.

Secant Modulus or Stiffness needed to elongate the sample 1% of its original length a to the elongation (or strain) of the specimen. 1% Se cant Modulas for l in. specimen =T/0.0l 100T v I Yield Stress This value was determined as the stress at the first major break in thestreSs strain curve and usually corresponds to the necking-in point.

Tensile Strength or Ultimate Strength Elongation" This value was determined as the extension of the specimen at the point of break or rupture.

L L, elongation 'X L length at rupture I L initial length of specimen.

Rupture Energy r This value was determined as the area under the entire stress-strain curve when the sample is subjected to tensil stress up to the rupture point.

Strain Rate This value is the rate at which the sample is-being elongated relative to its original dimension. Thus, if a 1 inch gauge length sample is used and the cross head of the testing apparatus is driven at a speed of 1 inch per minute, the strain rate is the ratio of gauge length to this speed or 1 inch divided by 1 inch per minute which is a rate of 1 inch per inch per minute. This value is reported hereinbelow as a percent, in which case the. ratio is multiplied by l00%. a

Body Voltage This involves measurement of the voltage built up on a person when walking on a carpet. The test is carried out according to the revised procedure established by the American Carpet lnstitutes Subcommittee on static electricity Aug. 13/68 and "approved by the American Carpet lnstitutes Technical Committee Aug. 19/68.

Volume Resistivity Current flow is measured through a 10 cm. length of 7 Volume resistivity L 1 ohm cms A Cross sectional polymer area cm L =length (10 cm) V applied voltage (1000) l current (amperes) Opacity Opacity is acomparative evaluation of individual fibers viewed against a black background under a low power microscope.

Lustre This is a subjective evaluation of the relative light re- :ctance level of yarn samples. Fiber containing the clic ester polymer to be evaluated may be'knitted to a test stocking or, alternatively; it may be imped, then tufted into a test carpet for observing stre.

' Relative Viscosity This is the ratio of the viscosity of a 1 weight per cent lution of the polymer (or fiber) in sulfuric acid, to at of the viscosity of the pure solvent. Viscosities are :asured at 20C using an Ostwald capillary viscome- Soiling I Fiber to be evaluated is either knitted into a test )cking or crimped and tufted into a test carpet. In this st, 5 inch square samples are fastened on the inner Ill of a cylinder which rotates about its axis, containstandard soiling material and ball bearings. After :atment, the degree of soiling may be rated visually, fore or after vacuuming Equipment used is a Cyanaid Soil Tester (Custom Scientific Instruments Inc. odel CS-79-0l2 Heat Stability Yarn samples are placed in an oven at 130C for 1 Fur. Yarn tenacity (grams/denier), yarn elongation to e break and yarn color are determined before .d after the oven exposure. Loss in tenacity or elongam or development of yellowness indicate the degree instability to heat.

Light Stability and Fastness Yarn samples, wound on a black card, are evaluated r tenacity and elongation before and after exposure Xenon arc light, using a glass filter, in an Atlas Elecc Devices Co. Weatherometer Model 600-WR. ass in tenacity or elongation over a 250 hour exposure riod indicates the degree of light instability.

Color fastness is determined by exposing, inthe foreing equipment, dyed samples of test stockings of the ver. Color change due to light exposure is judged by mparing exposed and unexposed portions of the me dyed stocking.

Extractables Yarn grams) are extracted with methanol in a xhlet apparatus for 8 hours. The methanol is then aporated, the weight of the residue representing the EXAMPLE 1 v A series ofthree blends (Nos.2, 3 fl lw ere made by first fluxing, an aromatic poly(hydroxy ether) made by the reaction of bisphenol A and epichlorhydrin and having recurring units of the formula:

The poly(hydroxy ether) had a molecular weight of about 30,000, a heat distortion temperature (ASTM D648) of 188F. at 264 psi and a specificgravi'tyof about 1.182. The poly(hydroxy ether) in each case was fluxed on a two-roll mill at a temperature as respectively shown in Table I below.

Then, a cyclic ester polymer of epsilon-caprolactone was added to each fluxing poly(hydroxy ether) in the proportions respectively set forth in Table l. The cyclic ester polymer (PCL) used in each case was prepared by dispersion polymerization in heptane of -epsilon-' caprolactone in the presence of 3% vinyl chloridelauryl methacrylate copolymer as interfacial agent and 0.1% of triisobutylaluminum as catalyst (percentages based on weight of caprolactone) and had a'reduced viscosity of l.89. After addition of the cyclic ester poly-v mer the resulting blends were milled at the temperatures for the times respectively given in Table I andwere sheeted off the mill and cooled. During milling of all of the blends, fluxing and banding were observed to be good and all exhibited quite acceptable bank .behavior. Also, the remaining milling characteristics were acceptable at the proper temperature.

A similar quantity of the poly(hydroxy ether) identified above was fluxed in the same manner at the temperature listed in Table I for the time similarly listed. No PCL was added to this control sample (No. l) which was sheeted off the mill after the designated milling time. Y

The resulting blends and control sample were then compression molded at 1500 to 2000 psi and 150C. for 10 seconds into plaques about to 30 mils thick. The plaques were then aged for about 8 days and then measured for physical properties, they results of which are given in Table I. The physical properties weremeasured again after 22 days aging at ambient temperatractables which is expressed as a percentage of the tures and the obtained values were in agreement with iginal yarn weight. the respective values given in Table I. -I'

TABLE I wuz PCL 0 l to 5,0 l9? Secant Modulus, psi* 166,000 l68,000 2l0,000 Yield Stress, psi 9200 8900 v Tensile Strength, psi 8300 7500 400 Elongation, 7: 280 280 1300 I Rupture Energy, in. lbs/in. 19,600 H.400 2,700

Izod Impact Strength." 2.06 1.92 l.0l, i fr.lbs./in. l Heat Distortion 87 82 '66- i Temperature, C. i V a .w Strain Rate. in./in./min. l:00 I00 1 )0, f Mllllng Temperature. C. l25 l20-l3() [BO-1 10"" bio-T30" Milling Time, min. 5 l0 l0... l0

I /r secam modulus values obtained at I071 strain rate. in./in./min. "ASTM 0256-56 ASTM D648-56 17 This example illustrates the surprising property of the PCL to blend well with the po1y(hydroxy ether). Visual observations of the l and 10% PCL (Nos. 2 and 3) indicated that these blends had better optical properties 18 This example also illustrates the production of uniform blends of polysulfone and PC. The blends Nos. 6 and 7 were more flexible than the control sample (No. illustrating the use of added PCL to flexibilize polysulthan the P y y y ether) alone withno PCL added 5 fone polymers. In addition, the blends are more easily (No. l This example also illustrates the flexibilization processed or fl d at elevated temperatures Modulus of p yt y y ether) y the addition f PCL to P values (stiffness) of the blends are far less than 'modu- Vide more flexible and tougher matenal- Sample lus values for polysulfone alone at moderately elevated the 50% blend (No. 4), exhibited very good adheslon temperatures f about or more to aluminum foil. All blends (Nos. 2, 3 and 4) were uni- 10 a form throughout and were more flexible than the con- EXAMPLE 3 Sample A series of six blends (Nos. 9-14) were made by flux- EXAMPLE 2 ing in a Brabender head a cyclic ester polymer and a polycarbonate made by the polymerization of bisphe- A Senes of two blends (NOS- 6 and were made by no] A with phosgene and having recurring units of the first fluxing in a Brabender head a cyclic ester polymer formula: and a polysulfone made by polymerizing bisphenol A and di(parachloropheny1) sulfone and having recurring units of the formula:

CH O 1 ii I 11 c 0Q- S 00-0 0H. 11

The polysulfone had a melt flow at 350C. of about 7.0 g/ a 44 p i S 8 Softening Point The polycarbonate had a high molecular weight, a spe- (ASTM D648) of about 34501:. at 264 P as detefcific gravity of about 1.2 (ASTM D-792), a flexural mined by Heat Deflection Temperature and a specific 3O d l f 340,000 i (ASTM-695), d a h di gravity of about 1.24. The cyclic ester polymer was tortion temperature of about 270C. at aload of 264 psi made from epsilon-caprolactone in the same manner as (ASTM-D648). The blends were fluxed and mill d in described in Example 1 and was Used in the amounts a Brabender head at a jacket temperature of 170 to shown in Table 11 below. The respective blends were 180C, and a polymer melt temperature at fluxing of fluxed for about 5 minutes at a temperature of 250C. about 220 to about 250C for blend No. 6 and a temperature of 230C. for blend Th li ester polymer was d i h using 3 190C jacket temperature 125 p tions respectively set forth in Table 111 below. The cyrotor Speed, and a 6 roller headclic ester polymer (PCL) used in each case was pre- Eaeh blend was compression molded into pared by polymerizing epsilon-caprolactone in the plaques having a thickness Of about 20 IO 30 mils. In 40 manner described in Example 1, The blends were addition, COfltfOl p q 0f the Same PP milledfor about 5 to about 10 minutes under the condimate thickness were Compression molded from Pellets tions given above and then were sheeted off the mill 0f the above-identified polysulfone P q were and cooled. The milling characteristics of all blends tested on an Instron tensile tester P y were good with little or no sticking to the surface of the properties and the results are respectively set forth in B b d h d, Table 11. A similar quantity of polycarbonate (No. 8) identi- TABLE I] fied above was fluxed in the same manner at the temperature and time listed above. No PCL was added to 5 6 7 this control sample, which was sheeted off the mill after the designated milling time. yg- 'i s psi, 39 The resulting blends and control sample were then Yield Stress psi 8900 compression molded into plaques 20 to 30 mils thick. g i g g s P $22 38 The plaques were then tested on an 1n stron tensi1e tesgfi 11900 8.500 4300 ter for physical properties, which are listed in Table 111 in.1bs./in. below. The add1t1on of PCL to the thermoplastic polyq e 20 100 100 mer at amounts of 20 to 50% flexibilizes the thermoplastic, giving rise to higher elongations and a softer I /1 secant modulus value obtained at 10% strain rate. in./in.lmin. o pos tio TABLE 111 Wt. 71 PCL 0 1 5 10 20 5O 1% Secant Modulus. psi* 171.000 150,000 167.000 164.000 140.000 62,500 39,000 Yield Stress. psi 8500 8000 9200 8300 7400 1950 Tensile Strength. psi 8700 8700 7400 5900 8100 3800 4500 Elongation. 220 230 53 45 270 470 1490 Rupture Energy. in.-1bs./in. 16.200 16.400 3800 2700 15.200 14,400 36,700 Strain Rate. in./in./min. 100 100 100 100 100 100 1% secanl modulus values obtained at 10% strain rate. in./in./min.

EXAMPLE 4 r A series of three blends (Nos. 16, 17 and 18) were i ade by fluxing on a two-r011 mill a cyclic ester poly.- er and a predominantly polyoxymethylene polymer I 1 thermoplastic polyoxyethylene polymer having a melting point rangerofz about 63 to 67C., a viscosity of about 8,000 to about 16,000centipoise as a aqueous solution at 2596, a specific gravity as a film of mining predominantly, Le 95 to 98 mol 5 about 1 .21 g/cc, and a reduced viscosity of about 4.9 ethylene units, cn o and 2 to 5 mol oxyethyl g g lfi l 21 55 gwncemratlon of gram P 100 Cl-l-O, d b 01 merizin trio W e zn e titii t h a r ri zill ari1ountet7tylrf2xide- This goly- The cyclic ester Polymer was used 'in adequate P ymethylene polymer had a melt index of about portions respectively producing the percentages of ms in 10 mins) a specific gravity of about 1410 10 PCL set forth in Table V below. The cyclic ester polyisTM 792-6OT) a flow temperature (ASTM 0569- mer (PCL) used in each Case was P p from p f about 345 and a melting poimof. about lon-caprolactone in the same manner as described in to about Example 1. The resulting blends were milled for about rhe'cyclic ester powmer (PCL) used was prepared 1 5 rninutes each at a temperature of 90 to 100C. The )m epsilomcapmlactone in the same manner as millllng characteristics of all blends were found to be ribed in Example 1 and was used in the proportions goo 313 fl T resutmg ieQe?11Z11 LblL1JZs Jd illflfiillifiifi 'ZZSZ 2 t e times an at t e tern era- .gg isz'e gin f lfagle I; below The mining behavigr for O manner as described above, at the same approximate 2 blends was found to be good and there was little or 23:5 32 52fi sag gggsd ig fhg gggfigi 52552 gqg sticking to the rolls of the two-r011 mill. l A similar quantity of the same poyoxymethylene l9 l)lW;1lfi1rln\;/21S sheeted off the mill after the designated h manner at a tern eram .g g gzi g 1:3 minutes NO f was A similar quantity of the cyclic ester polymer identided to this control sample which was sheeted off the fled above was fluxed in the Same manner at the same 11 after the designated milling timg temperature and for the same period of time as listed The resulting blends and the control sample were above- This control Sample cofltained H0 in compression molded into plaques about 20 to E Y Yt QI Z ih O f gjli Off the after the est na e e ls thlck' The physlcal proPemes of the plaques were 30 TEe resultin blends and control sam les were then :asured on an Instron tensile tester and the measureg P mts are given in Table IV below compression molded mto plaques about 20 to 30 mils TABLE IV PCL 0 10 90 Secant Modulus, psi* 170.000 143.000 67.000 33,000 21d Stress. psi nsile Strength. psi 7600 6500 3600 1400 ngation, 7: 1 28 90 20 1200 pture Energy. in.-1bs./in. 1940 5700 650 25000 ain Rate, in./in./min. 100 100 100 100 lling Temperature, C. about 160 160 160 160 lling Time, min. about 5 5 10 10 l secanl modulus values obtained at 10% strain rate. in./in./min.

EXAMPLE 5 50 thick. The plaques were then tested for physical properties on an lnstron tensile tester and the measurements are given in Table V below.

TABLE V 7: PCL 0 l 2 I 5 10 20 50 Rupture Energy, 5165 17802 15421 29235 24932 29953 33281 37536 46946 71887 in.-1bs./in. 1 1 Elongation, 7: 370 1468 1269 2254 1811 1958 1633 1549 1729 1930 Tensile Strength. 1229 1247 1110 1383 1500 1930 3557 4217 6219 7078 P Yield Stress, Si 1790 1543 1631 1464 1640 1654 1825 1581 1589 1674 Sccant Modu us. 3.34X10 315x10 3.32X10 334x10" 3.57X10; 295x10 321x10 2.15X10 1.64X10 1.85X10 dyncs/cm 1 1 I Strain Rate 100 100 100 100 100 100 i 100 100: I 100 100 These data illustrate the improvement in physical properties of the blends over polyoxyethylene alone.

The blends and the control samplecontaining no PCL were then tested in a series of swelling studies. In these tests, a plaque of each blend and the control sample measuring about 1 inch by A inch was placed in a test tube with 3 cc. of distilled water and allowed to soak while being observed. The results are listed below.

% PCL deformed in minutes, disintegrated in 65 minutes, and completely dissolved in 3 hours.

1% PCL deformed in 5 minutes, disintegrated in 65 minutes, but did not completely dissolve 2% PCL deformed in 5 minutes, disintegrated in 65 minutes, but did not completely dissolve.

5% PCL deformed in 5 minutes, disintegrated in 65 minutes, but did not completely dissolve.

% PCL deformed in 5 minutes, disintegrated in 24 hours, but did not completely dissolve.

20% PCL slightly deformed in 17 minutes, did not disintegrate or dissolve.

50% PCL no visible change during or after a 24- hour soaking period.

75% PCL no visible change during or after a 24- hour soaking period.

90% PCL no visible change during or, after a 24- hour soaking period.

The percent weight losses for the 20% PCL, 50% PCL and 75% PCL blends after the above-described soaking and then drying for 29 hours in vacuum at room temperature were measured and were found to be, respectively, 74 weight 45 weight and 12 weight This test illustrates the waterproofness imparted to polyoxyethylene by the presence of PCL. In addition, it illustrates that the polyoxyethylene polymer may be leached from the blend leaving a porous or microporous matrix, which is largely PCL.

The blends containing 1, 2, 5, l0 and 20% PC] and the control sample containing no PCL were tested in a stress endurance testing device. The test specimens were cut 7 /2 inches long and /4 inch wide. Marks were made on each specimen 5 1 H16 inches apart and each specimen was installed in the tester and locked in position at the marks made on them. The thickness of each specimen was 10 to mils. The tester was then closed which stretched the film approximately 5%. This amount of stretch was maintained until the film broke. Four to six specimens were used iin each group. The results are given below:

0% PCL All specimens broke after 3 to 5 minutes.

1% PCL All specimens did not break for 14 to 2l minutes.

2% PCL All specimens did not break for 20 to 30 minutes.

5% PCL All specimens did not break for l to 2 hours. One specimen did not break but only necked when stretched for approximately 40 hours.

10% PCL All specimens did not break for 35 minutes to 45 minutes. One specimenidid not break for 72 hours. One specimen only slightly necked when stretched for about 192 hours.

20% PCL All specimens did not break for 30 minutes to 5 hours. One specimen did not break but only slightly necked when stretched approximately. 20 hours.

This test illustrates the toughness or stress endurance imparted by PCL to the polyoxyethylene.

g EXAMPLE G I As'eries'ofthree blends (Nos. 29-3l )were made from a cyclic ester polymer and a maleic'anhydridemethyl vinyl ether-copolymer of m'edi'ummolecular weighthavinga softening point range of about 200 to 225C., a specific viscosity of 'l.0 to 1.4 dl/g at -a concentration of l copolymer dissolved in ml methyl ethyl ketone at 25C. and a specific gravity as a film of 1.37. t

The cyclic ester polymer (PCL used in each case was prepared in the same manner as described in Ex-' ample l and the amount used was sufficient to provide the percentages listed in Table VI below. I

In ,making the 10% PCL blend, the copolymer was added to the mill first and then the PCL but milling behavior was poor to fair in most respects although it was good respecting bank and hot strength. Therefore, in making the 50% PCL and 90% PCL blends, the PCL was first addedv to the mill and then the copolymer and milling behavior was very much improved in all respects. The resulting blends were milled on a two-roll mill for about 5 minutes at to C. The blends were then compression molded into plaques about 20 to 30 mils thick.

Attempts were made to compression mold the control sample of the copolymer containing no PCL. However, gas coming off of the sample during heating forced the molding plates apart and prevented molding even under a pressure of 20,000 psi at a temperature of 215C. for 2 minutes. The control sample shrank and turned brown in the attempts to ,compression mold it.

The plaques formed from the blends were tested in an lnstron tensile tester and the physical properties are given in Table VI below.

TABLE VI- 7r PCL 10 50 r 90 Rupture Energy.

in.lbs.lin. 53 847 21790 Elongation, 2 .36 H52 Tensile Strength. psi 2942 2494 2690 Yield Stress, psi 1920 Secant Modulus,

dynes/cm. 12.53Xl0 5.03Xl0 244x10 Note: Data obtained at 100% strain rate.

This example illustrates the modification of a difficultly moldable polymer in accordance with this invention to render it more easily moldable.

EXAMPLE 7 about L02 'g/ml, and a specific rotation in chloroform with 589 rnillimicron light at 25C. of about 2C.

The cyclic ester polymer was used in sufficient amounts to provide the proportions respectively set forth in Table VI] below. The cyclic ester polymer 23 PCL) used in each case was prepared from epsilonaprolactone in the same manner as described in Exmple l. The resulting blends were milled at a temperaire of about 50 to about 90C. for approximate1ye5 iinutes, and then sheeted off of the mill and c l d, were tested in an lnstron tensile tester. The physical lilling behavior for all blends was quite good. properties are given below: e 1 1 A similar quantity of the cellulose tridecanoate iden- TABLE VI" fied above was fluxed in the same manner at a temperture of about 90C. for about 5 minutes. No PCL was 36 37 dded to this control sample.

The resulting blends and control samplexwere then 3:3 En y 10 5 ompression molded into plaques about 20 to 30 mils time in, g 10265 551 iick. The plaques were then tested in an Instron tenggle gj f l gi @32 1e tester and the physical properties are given in Table -1.3 Moduglus E 09 123M109 '11 below.

N E TABLE VII 1):: obtained at 100% strain rate v 32 33 35 EXAMPLE 9' :3; Energy 4 ag i2 23 Three blends were prepared each containing 400 in./lbs ./in. parts of nylon 6 pellets containing titanium dioxide 68 173 1668 and, respectively, 10.29 parts, 21.05 'parts', and 44.45 8; Strength 590 487 836 6040 parts of a cyclic ester polymer ('PCL) of epsilonield Stress. P 771 a l a I006v 9 I459 9 caprolactone prepared in the same manner as defifi es ciiii 9.6mm 174x10 119x10 "82x10 scribed in Example 1, except 0.3% c'atalyst was used and the resulting'cyclic ester polymer had a reduced ate: r viscosity of 1.98. Nylon 6 of this'type was purchased from Courtaulds as Dull 704, contains TiO and has a a relative viscosity without the TiO of 2.26 in sulfuric well as most h sical ro erties'of the blends impared by dlssolvmg the cychc ester polymer m 400 d h p y h bl d parts of methylene chloride. Each of the resulting soluf as t 6 amount 0 m t 8 en S wasm' tions was then contacted with the nylon pellets and the easedresulting mixture was then stirred and dried to effect a EXAMPLE 8 sullastantial coating of the nylon with'the cyclic ester po ymer. i gnl's gfl giliz fstg izl'sz'ng i g 1:3 oi e gi l zi Ah control samlple of the same nylo: 16 was :leateid wit an e uiva ent amount 0 met ene -c ori e iprolactone (same as used in Example 1) and nylon which contained no PCL a: g Th i ii of 4 these blends and control sample were"then mixed v m a e e e f wa with an equal weight of the same nylon 6 but which had lreslone Nylon 6 yp Melt "ldlces not been treated with MeCl or -PCL.Thus the final 15 temperatures were found to be as follows: blends contained 1.25, 2.5 and 5% PCL. Each of the blends and control sample were then spun into multifil- Temp Meltindex ament yarns using a spinning head temperature of 265C. and a polymer temperature of 245C. The spin- 260C. 23.5 neret had 25 .holes of 0.020 in. diameter. The measured gag yarn take-up velocity was 300 feet per minute and the 290C. 64.0 5 orifice velocity was 5 feet per minute giving a meltgg draw ratio of to 1. Spinning behavior was good with the 0, 1.25 and 2.5% PCL blends. The cold-drawing or stretch data are given in Table IX. The stretching aid he powder blend was heated to melt the powder while in the colddrawing process was 2. 120C. pin. The physinder a nitrogen atmosphere and stirred until the blend 55 cal properties of these spun yarns are listed in Table IX.

TABLE 1X mpct 0 l 1.25.1 4 e 2.5 '5

' Celd Draw Data Feed rate ft/min. 100 ft/min. 100 ft/min. lOO ft/min. galstte upgate 4803fggmin. 5004t5/0min. 4803fgmim 420 fgmin.

I re c I 3 AverageDenier 178' 171' 179' 207 Teiiac ty gm./ 1 7.2 6.9 6.2 5.0 t

enier y g p longation 15.2 15.4 16.9 18.9 l IIIQSS, up gmJdenier 43.6 44.0 37.0 31.6

was thoroughly 'mixed and uniform. The blend was then cooled to room temperature under a nitrogen atmosphere. Plaques about 20 to 30 rnils" thick were compression molded from each blend and these plaques 25 26 Regarding the physical properties in Table 1, these TABLE X were determined with an Instron tensile tester using a 10 in. gauge length and a 6 in. per min. rate of exten- 43 44 45 sion. The extension is the extension at the first filament break after which the load does not increase. The 7l PCL 25 50 90 figures given in Table X are averages of 5 tests. g gs fi f y- 5 53 5082 1 The 95% Nylon-6/5% PCL fibers had an 8.9% shrinkg'gazstgg psi 3170 is. age in boiling water, a 7.4% shrinkage in 150C. air, YiBIdSIWSS- P 9 1916 9 and 14.4% shrinkage in 200C. air. No shrinkage was 10 32251239 Mlxlo 591x"? 289x) measured on the other three samples.

The spun fibers were dyed with si ht-mined at um strain rate. 1. Celliton Fast Navy Blue BA, a disperse dyestuff 2. Celliton Fast Red GGA, a disperse dyestuff l5 3. Celliton Fast Black BA, a disperse dyestuff 4. Capracyl Red B, a premetallized dyestuff. EXAMPLE H A series of four blends were made by fluxing on a All samples had excellent y P P however, the two-roll mill a cyclic ester polymer and an acetylated PCL COmainning blends had Slightly deeper colorsethyl cellulose having an M. S. of 1.1 (average of 1.1 mols of ethylene oxide chemically added to each anhy- EXAMPLE 10 droglucose unit), a D. S. of 1.6 (an average of 1.6 acetyl groups substituted for hydroxyl hydrogen per anhy- A senes P three Blends were made by a droglucose unit) and having a reduced viscosity of 3.62 l i 3 Cychc ester polymer and a Snlbene' dl/g at a concentration of 0.2 g acetylated ethyl celluacrylomtrlle copolymerlose dissolved in 100 ml dimethylsulfoxide at C.

The acrylonitrile-stilbene copolymer was prepared by solution polymerization in dimethyl formamide. The The cychc faster polymer w amounts copolymer composition by monomer charge was 33/67 30 quate to provide the proportions listed in Table X1 beacrylonitrile-stilbene on a weight basis. Nitrogen analy cychc ester polymer (PCL) used was made sis showed that composition obtained was 49.7/51.3 m ep sflon'caprolactone m h Same manner acrylonitrile-stilbene on a weight basis. The cataalysts Scnbed m Example The resultmgflends were mued used were 0.5% dibenzoylperoxide and 0.5% azobisfor about 5 mmutes at about and each [isobutyronitrile]. Reduced viscosity of the copolymer 35 blend l Off of the and l 'f R was in dimethylformamide at was 036 dl/gm when noted dur ng milling that those blends containing more measured at a concentration of 0.2 gm/lOO ml. The cy- PCL provlded bette r behavlor At 1 PCL and die ester polymer (PCL) was made from epsilorb more, fluxing, banding, bank and dispersion charactercaprolactone in the manner described in Example 1 Sues were goodand was used in amounts adequate to provide the pro- 40 portions of PCL respectively set forth in Table X be- The blends as well as a control sample containing no low. The resulting blends were milled for 5 minutes at PCL were compression molded under a pressure of about 175C. During milling, it was noted that fluxing, 5000 psi for the control sample and the 1% blend and dispersion and banding were quite good. After the des- 1000 psi for the remaining blends. The compression ignated milling time, the blends were sheeted off of the molding temperature was 170 to 190C. and molding mill and cooled. Plaques were compression molded time was 10 seconds. Each of the resulting plaques, from each of the milled blends and the tensile properabout 20 to 30 mils thick, was then tested in an lnstron ties were determined with an Instron tensile tester. The ten il tester and the physical properties are listed in tensile properties are given in the 'table below. Table X1 below.

TABLE XI 46 47 4s 49 so PCL 0 1 10 50 Rupture Energy, in.-lbs./in. 280 122 51 33 7409 Elongation. 6 4 3 3 473 Tensile Strength. psi 5936 5262 2884 1667 1628 Yield Stress, psi 1642 Secant Modulus. dynes/cm Y l2.25 l0 13.47Xl0 4.9X109 258x10 Note:

Data obtained at 3 strain rate.

27 EXAMPLE 12 lose alone and was tough and leathery. The blend 1 uld be molded at temperatures of about 100 to EXAMPLE 13 A series of four blends (Nos. 52-55) were made from llulose triacetate and a cyclic ester polymer, PCL. 1e cyclic ester polymer used was prepared by the bulk lymerization of epsilon-caprolactone using 0.2 :ight percent stannous octoate as catalyst. This subtntial homopolymer had a reduced viscosity of 0.65

Arnel cellulose triacetate fibers (Celanese, 200 deer, filament 52, SH Luster, type bright) were used as e cellulose triacetate. This type of fiber has a melting nge at about 572F., a specific gravity of about 1.3 1d is further described in Textile World, 1962, Man- EXAMPLE 14 A series of two blends (Nos. 57 and 58) were made from cellulose diacetate and a cyclic ester polymer (PCL). The cyclic ester polymer was prepared by bulk polymerization of epsilon-caprolactone using stannous octoate as catalyst. The substantial homopolymer had a reduced viscosity of 0.65 dl/gm.

The cellulose diacetate used was an Eastman product having an'acetyl content of 40% and an ASTM viscos- 'ity of 25.

Solutions of the two blends and a control solution '(No. 56) containing cellulose diacetate but no PCL were prepared in acetone in the weight ratios indicated in Table Xlll. The solutions were warmed to about 55C. to aid in effecting solution. Thin films were then cast on Teflon. The films were covered during drying. When dry, portions of the films were tested in an Instron tensile tester to determine tensile properties which are summarized in Table XIII.

Film clarity was judged by visual observation. All films were smooth. The data show that low amounts of PCL will plasticize cellulose diacetate. The haze development permits a more opaque fiber with greater hiding power to be spun from such blends.

ade Fiber Chart. The fibers were washed twice with TABLE m )propanol to scour them of lusterants and other mate- 30 11s and then dried ina vacuum oven to remove excess 56 57 residual isopropanol.

Solutions of the blends of scoured fibers and the lose mace-me i IL, and a control solutlon of the scoured fibers (No. parts Acetone 90 90 90 containing no PCL, were prepared in methylene M d I 00 i0 20 1loride in the weight ratios indicated in Table x11. The fg g f 3:; 13,530 $288 3 lutions were warmed slightly to effect solution. Thin Elongation, 7: 6 18 4 ms were then cast onto Teflon and dried for about 1 ;g i; E 600 1300 -O- ur or more. Portions of the thin films were tested in mm Clarity Clear Very Slight 1 Instron tensile tester to determine tensile properties. 40 slight haze haze :sults are shown 1n Table XII. The film clarity given in'Table Xll was judged by vial observation. There is a definite increase in haze as e PCL content is increased. All films are very smooth EXAMPLE 15 ;cept'for the 30% PCL film which is rough. The 30% IL film absorbed fountain pen inkand, after dry, ."itings on' it could not be easily rubbed off. They 1uld be easily rubbed off of the other films. The haze crease in the blends with increasing PCL permits the anufacture of a more opaque fiber, i.e. one which has greater hiding capacity. In addition, the tensile propties of the 10, 20 and 25% PCL-containing blends ow that PCL is acting as a polymeric plasticizer for e cellulose triacetate permitting a tougher fiber when ends of the two materials are spun into a fiber.

A series of five blends (Nos. -64) were made from a chlorinated polyether and a cyclic ester polymer (PCL).

Penton (Hercules Powder Co., Inc.) was the chlorinated polyether used. lts monomer, which is a chlorinated oxetane, is synthesized from pentaerythritol. The chlorinated polyether had a molecular weight average range of 250,000 to 350,000. It is a linear thermoplastic polymer that is crystalline in nature and has recurring units of the formula:

TABLE XI! rts PCL 0 l 2 5 6 rts Cellulose Triacetate 9 9 8 l5 l4 rts MeCl 9O 90 90 90 PCL 0 10 20 25 30 l Secant Modulus, psi 210,000 208,000 166,000 151,000 153,000 :nsile Strength, psi 9,700 9,100 7,200 9,200 5,000 ongation, 7! l4 l5 26 22 5 1pture Energy, in.-lbs./in. l 1060 1500 1780 .m Clarity Clear Clear but Clear but Clear but Clear but slightly somewhat quite hazy very hazy hazy hazy 1 CPI-2C1 o--CHi-- ---CH2 The cyclic ester polymer used was prepared by the dispersion polymerization of epsilon-caprolactone in heptane using a vinyl chloride/lauryl methacrylate copolymer as the interfacial agent. Catalyst was triiso-' butylaluminum. Reduced viscosity was 1.88 dl/gm.

The above polymers were blended in the ratios indicated in Table XIV in a Brabender head with the jacket temperature set at 220C. for 5 to minutes. After blending the polymer mixtures were removed from the Brabender and plaques were compression molded. Plaques as control samples (NO. 59) were also compression molded from the chlorinated polyether which contained no PCL. Strips cut from these plaques were used to determine the tensile properties which are summarized in Table XIV using an lnstron tensile tester. The glass transition temperatures, Tg, shown in the table were taken from the maximum in the loss component of the complex shear modulus which was determined through data taken with a recording torsion pendulum. Frequency of measurement at Tg was about 1 to 2 cycles per second. I

The results in Table XIV show that PCL is a polymeric plasticizer for chlorinated polyether. Increasing amounts of PCL produced a tougher product.

,1. .30 about 5. minutes. Milling behavior: fluxing,,banding, bank'and dispersion were good for the control sampleand for all blends. Roll release and hot strength were poor for the control sampleand for the blends. After hot blending,,the blends and control sample were removed from the mill and compression molded into plaques.

Physical properties of the blends and the control sample were determined with an lnstron tensile tester. These physical properties are given in Table XV. The properties were determined on strips about A inch wide, 1 inch long (gauge length) and about 0.030 inch thick. The glass transition temperatures, Tg, were determined as described in Example 15 PCL have impoved creep resistance, improved moldability and formability, and improved low temperature properties. PCL is a polymeric plasticizer for the polyepichlorohydrin elastomers.

TABLE XIV v. PCL 0 i0 25 so 75 90 17: Secant Modulus. psi 88,000 70,000 25,000 33,000 30,000 25,000 Tensile Strength, psi 3,100 3,700 3,700 3,700 5,200 5,300 Elongation, 7: 105 120 940 1,000 1,800 1,500 Rupture Energy, in.-lbs./in. 4,100 4,100 23,500 27,000 45,000 40,000

g, +18 10 ''50 Milling Temperature, C. Not milled 220 220 220 220 220 (Plaque v Milling Time, min. merely 5-10 5 5l0 5 5-10 molded.)

EXAMPLE 16 The blends containing and especially 90%, or

A series of three blends (Nos. 66-68 we're made from a thermoplastic poly(epichlorhydrin) and a cyclic ester polymer (PCL) prepared from epsiloncaprolactone in the manner described in Example 1. The poly(epichlorhydrin) used was a commercial product sold by B. F. Goodrich Co. under the name HY- DRIN 100. It contained recurring units of the formula:

CH Cl HCH O and had a specific gravity of about l.36..The polymer had a reduced viscosity of about 2 dl/gmwhen measured in dimethylformamide at 30C. anda concentration of 0.2 gm/lOO ml.

Blends of these two polymers and a poly(epichlorhydrin) control sample with-no PCL (No. 65) were milled on a two-roll mill at 120C. using a milling time of EXAMPLE 17 A series of three blends (Nos. -72) were made from a thermoplastic epichlorhydrin-ethylene oxide copolymer and a cyclic ester polymer (PCL) prepared from epsilon-caprolactone in the same manner as described in Example 1. The epichlorhydrin-ethylene oxide copolymer used was a commercial product, HY-

DRIN 200, sold by B. F. Goodrich Co. it contained recurring units of the formulas: I

31 nd had a specific viscosity of 1.27. The polymer had reduced viscosity of about 3.3 dl/gmwhen measured; 1 dimethylforrnam'ide 'at'30fC. and aconcentrationof .2gmperlmL' Blends of these two polymers and a copolymer con- 'ol sample (No. 69) containing no PCL were milled on two-roll mill at 120C. using a milling time of'5 mintes. Milling behavior in fluxing, banding and disperon were good. Bank, roll release and hot strength 'ere considerably improved in the blends as compared the control sample and thus the hot proces'sability of re blends was considerably better than that of the con- '01 sample. After hot blending the control samples and re blends were compression molded into plaques.

Physical properties of' the blends were determined ith an lnstron tensile tester. These physical properties re given in Table XVI. The properties were deterlined on strips about A inch wide, 1 inch long, and .030 inch thick. The glass transition temperatures, Tg,

ere determined as described in Example 15. I

TABLE XVI PCL 0 10 50 90 7t Secant Modulus, psi 50 530 7700 29,000 ensile Strength. psi 80 2600 6500 longation, 7: 230 670 1500 1900 upture Energy, 50 460 22,400 58,000

in.lbs.lin. C. 35 40 45 -49 These results show that addition of PCL improves the reep resistance of the copolymer, improves moldabily and formability of the copolymer, and improves the w temperature properties of the copolymer.

The blends containing 50%, and especially 90%, or

lore of PCL are useful as low melt adhesives having' nproved cohesive strength. Moreover, the blends conlining 40% or more PCL are useful in the production ffilms which can be oriented by stretching at elevated :mperatures below the melting point of the blends and EXAMPLE 18 A particulate cyclic ester polymer (PCL) made by ispersion polymerization of epsilon-caprolactone in IC presence of vinyl chloride-lauryl methacrylate coalymer as interfacial agent and triisobutylaluminum as italyst and having a reduced viscosity of 0.6 was .ixed in different proportions as shown in Table XVII ith cellulose acetate butyrate 10th Second butyrate, astman Chemical Products) containing 13 percent ac- ;al and 37 percent butyral and havinga viscosity of :out 0.1 seconds as determined ASTM m'eth dD} 343-54T. These mixtures were prepared dissolving 1611 of the polymers in 2-nitropropane to give'soluans containing about 20 percent polymer. Admixtures :these solutions were then prepared in .the proporans shown in TAble XVII hereinafter. Films of these mixed solutions were cast on glass plates giving dried films about 5 to 6 mils thick. The tensile properties of the dried films weredetermined and the resulting data are given in TAble XVII.

The films containing less than about 50 percent of PCL were clear, indicating compatibility of PCL and cellulose acetate butyrate in this range of compositions. Films with about 50 percent PCL or higher were hazy. Films containing less than about 10 percent PCL were too brittle tobe removed intact from the glass plates for testing.

The demonstrated compatibility of PCL with cellulose acetate butyrate indicates the wide scope of applications of cyclic ester polymers as modifiers for cellulosic polymers. Cellulosic polymers are, of course, used in a wide variety of applications, such as, molded articles, protective coatings, paints, and inks, to mention only a few.

EXAMPLE 19 The cyclic ester polymer (PCL) used was a homopolymer prepared by the dispersion process using heptane as the nonsolvent and 5% of a vinyl chloride/laurylmethacrylate copolymer as the interfacial agent. Catalyst was 0.6% dibutyl zinc. Reduced viscosity of the PCL was 3.17.

The polyurethane used was made from 1 mole polyol, 2 moles MDI and 1 mole 1,4-butanediol. The polyol is a 2000 number average molecular weight polycaprolactone diol that is prepared from epsiloncaprolactone using diethylene glycol as the initiator and is hydroxy terminated on both ends. MDI is 4,4'-diphenylmethane diisocyanate. The polyurethane was prepared in the following manner. The polyol and 1,4- butane diol are mixed and heated to 140C. Then the MDI is, added and after mixing well (lor 2 min. after the MDI addition) the system is placed in a forced-air oven set at 180C. for 1 hour to cure. After this the system is cooled to room temperature and granulated. The result is a thermoplastic polyurethane having a reduced viscosity of about 0.8 when measured in dimethylformamide at 30C. and a concentration of 0.2 gm per ml. 16 parts of PCL and 4 parts of the polyurethane were blended on a two-roll mill for 5 minutes at C. Milling behavior was good although there was some sticking to' the mill rolls. After blending the mixture was removed'from the mill, cooled, and then compression molded into plaques at C. and 1000 psi for 10 sec. The physical properties of the blend are compared with those of a control sample of the same polyurethane containing no PCL in Table XVlll. Approximate specimen size was V4 in. X l in. X 0.030 in.

TABLE XV l These data indicate that a more extensible and a softer (as shown by tensile modulus) material is made when 7r PCL 80 PCL is blended with the polyurethane without major I Secand Modulus psi 860 25 000 changes in hardness, tensile strength, tear, compression Tensile Strength, psi 5000 6:000 Set, 01' resilience. z gh fg Si 18 5o Substantially similar results are obtained as in respec- Rupture EnrZ inJbs/in. 1000 tively Examples 1-19 when the substantial homopolymers of, and copolymers of two or more of, the follow- Oriented films of the blend are uite clear and stron Such blends or similar blends are useful as heat shrinli cychc esters are respecnilely substituted for the epable acka in films silon-caprolactone polymer 1n each of these examples:

p g g delta-valerolactone, zetaenantholactone, eta- EXAMPLE 2O caprylolactone, monomethyl-delta-valerollactone, mo- The cyclic ester polymer (PCL) used was a blend of nOlifXyLdeltT-vilemlmmne g i four substantial homopolymers prepared by the dispereplsl olllcapro ac g i d l lmolnomet 3 i sion polymerization of epsilon-caprolactone in heptane Va f actone let e tava actone y using a vinyl chloride/lauryl methacrylate copolymer as epsllon'caprolactone and monolsopropoxyepllon' the interfacial agent. Three of the substantial homopolcaprolactone' ymers were prepared using triisobutylaluminum as the catalyst, and one was prepared with dibutylzinc as the 20 catalyst. The blend had a reduced viscosity of about 1.4 dl/gm.

The polyurethane used was a thermoplastic elastomer prepared from 1 mole polyol, 1.95 moles MDI, and EXAMPLE 21 1 mole of ls'pemanediol' The polyol was a 2000 numn To a reaction vessel containin 1000 rams of a 01 ber average molecular weight polycaprolactone diol g g y that was prepared from epsiloncaprolactone using 1,4- oxyethylefle glycol havmg an rage molecular weight butanediol as the initiator and was hydroxy terminated of approxlmately 6000 heated to about 65 m 3 Intro on both ends. MDI is 4,4-diphenylmethane diisocyagen atmosphere th re were adfied 887 gramS of aque' am The polyurethane was prepared in the following ous 50 percent sodium hydroxlde solutlon. The resultmanner After mixing the p 01y o1 and 1 p em an e di 01 at mg admixture was stirred until solution resulted. Thereabout 145C the MDlwaS added After mixing we" (1 after a 109 gram portion of this solution was trans or 2 minutesafter the MDI addition) the system was ferred to another vessel and heated to 95C. in a nitroplaced in a forced air oven set at 180C. for 1 hour to gen ajtmosphere and 2,88 grams of dlglycldyl ether of polymerize. After this, the system was cooled to room y yp y )propane Were quickly added, temperature and granulated. The result was a thermowith fi T1118 amPUm corresponds to molar plastic polyurethane that had an intrinsic viscosity (i.e. of 05:1 of the dlglyudyl ether to the P y Y Y the extrapolation of reduced viscosity values to zero g y Thegeafteflfle temperatllre was held Wlthm f concentration) of 0.86 dl./gm. when measured in dirange of 95 I0 110 C for u s. and the reactlon methylformamide at 30C. 40 mixture was allowed to cool to room temperature and The p and polyurethane were blended on solidify. The solid material was a tan-colored wax roll mill at 140C. for about 5 minutes. The milling beh C melted at 60C. This dihydroxyl-terminated havior was good regarding fluxing, banding, and disperproduct was characterized by a polymeric chain having sion. There was some rolling in regard to the bank bethree 'polyoxyethylene segments therein which averhavior. Roll release was poor, and hot strength of blend aged about 6,000 molecular weight each, said chain was fair. Details of blend compositions and physical being interspersed with the two phenylenero erties of the blends are given in Table I as compropylidenephenylene moieties from the di lycid ldip p g Y pared to those of the polyurethane containing no PCL. ether reactant.

TABLE XIX Parts Polyurethane 150.0 142.5 135.0 120.0 105.0 Parts PCL 0 7.5 15.0 30.0 45.0 PCL 0 5 10 20 30 Hardness, Shore A (ASTM D224064T) 86 86 Hardness, Shore D (ASTM D2240-64T) 44 46 Tensile Modulus* 1587 1507 1119 1311 1510 300% Tensile Modulus* 2578 2404 1929 1843 1855 Tensile Strength" 3148 2940 2989 3253 3433 Ultimate Elongation* 477 455 530 608 645 Tear Resistance Die C (ASTM D624-54) 728 678 598 670 676 Compression Set. B i (ASTM D395-6l, 62 63 60 64 60 Method B. 22 hrs. at 158F.) Rebound Resilience, '7: 34 37 34 36 39 (Zwick & Co.. Model 251E rebound pendulum "ASTM D4 1 2 66 EXAMPLE 22 Three hundred grams of epsilon-caprolactone and tree hundred grams .of the hydroxyl-terminated polyther compound of Example 21 supra were added to a 000 milliliter, 4.-neck flask, equipped with a thermomter and stirrer. The system was sparged with nitrogen, eated to 120C., and again sparged for about an hour 'ith nitrogen. Thereafter 0.3 gram of stannous diocmoate was added and the resulting reaction mixture eated to 180C. and held at this temperature for ours. During the entire period, the reaction mixture as maintained under nitrogen. When cooled to room :mperat ure, there was obtained an opaque, white crysilline, polymeric product. Thereafter, this polymeric roduct was heated to 180C. and held at this temperaire for 1 hour under vacuum, e.g., about 1 mm. of Hg. he polymeric product was then cooled toroom temerature dissolved in benzene, and precipitated and 'ashed with hexane. There was obtained 575 grams of fine white powdery block polymer having an ABA Jnfiguration in which the A blocks are recurring xypentamethylenecarbonyl units and the B block rep- :sents the product of Example 21 (without the termial hydroxylic hydrogen ,atoms).

To test water solubility 6.6 of this ABA block polyieric product .was placed in 70,2 grams of, distilled ater and stirred overnight. After settling an aliquot of ie'supernatant liquid, i.e., 6. 9 grams, was'removed 3d dried to constant weight. The residue weighed .027 gram indicating that virtually no part offthe block olymeric product was water soluble reconfirming that re desired reaction had taken place.

EXAMPLE 23 Three hundred grams of epsilon-caprolactone and tree hundred grams ofpolyoxyethyleneglycol having 1 average'molecular weight of about 6,000 were ided to a 1000 milliliter, 4-neck flask, equipped with thermometer and stirrer. The system'was sparged ith nitrogen, heated to 115C, and again sparged for sent an hour with nitrogen. Thereafter 0.25 gram of annous dioctanoate was added and the resulting reacon mixture heated to 180C and held at this'temperalie for 10 hours. During the entire period, the reaction .ixture was maintained under nitrogen. When cooled I room temperature, there was obtained an opaque, hite crystalline, polymeric product. Thereafter, this alymeric product was heated to 180C. and held at iis temperature for 1 hour under vacuun, e.g., about mm. of Hg. The polymeric product was cooled to om temperature, dissolved in benzene, and precipited and washed with hexane. There was obtained a )lld white block polymer having an ABA configuraan in which the A blocks are recurring oxypentameiylenecarbonyl units and in which the B block repre- :nts recurring oxyethylene units.

EXAMPLE 24 Epsilon-caprolactone 1000 parts by weight) and )lyoxyethylene glycol having an average molecular eight of about 3000 (300 parts by weight) were added a reaction vessel. Stannous dioctanoate (1.0 part by eight) was added thereto. The vessel then was placed an oil bath maintained at 180C. for a period of 24 Jurs. Upon cooling to room temperature the resulting :action product mixture was dissolved in benzene, to]

EXAMPLE 25 =-ln-a manner similar to Example 24 supra, when methyl-epsilon-caprolactone is used in lieu of epsiloncaprolactone, there is obtained a water-insoluble, white, solid block polymer.

EXAMPLE 26 Epsilon-caprolactone (100 parts by weight) and the monomethyl ether of polyoxyethylene glycol having an average molecular weightof about 4000 (80 parts by weight) were added to a reaction vessel which was sparged with nitrogen, heated to l20C., and again sparged for about an hour with nitrogen. Thereafter 0.2 part by weight of stannous dioctanoate was added and the resulting reaction mixture was heated to l80C. under nitrogen and held at this temperature for 8 hours. When cooled to room temperature, there was obtained a water-insoluble, white solid block polymeric product having an AB configuration in which the A block represents recurring oxypentamethylenecarbonyl units and in which the B blockrepresents recurring oxyethylene units.

' EXAMPLES 27-32 Five blends of Nylon 6 and the cyclic ester polymer prepared in the manner set out in Example 22 were spun'into multifilament yarns according to the proce dure indicated previously. The volume resistivity and opacity of-carpets made from such yarns were then determined and'compared with a control which contained no cyclic ester polymer. The results are set out in Table XX below.

' TABLE xx' EXAMPLE cvcuc VOLUME ESTER NO. POLYMER; RESlSTlVlTY OPACITY m 5 wt (ohm-cm) 27 CONTROL 2.2 x 10- 6 28 (z) 1.2 X 1O 29 1.5 10- 30 3.8 x 10- 3 3l W 5.6 10- 2 32 8.3 X 10' l Cyclic ester polymer is an ABA block polymer prepared according to the procedure set out in Example 22.

ABA block polymer in which the A blocks represent 80 wt. recurring oxypentamethycarbonyl units and in which the B block represents about 20 wt. /z recurring oxyethylene units prepared as noted in Example 21.

Same as footnote (2) except that the A blocks represent 50 wt. l: and the B block represents 50 wt. /r.

m Same as footnote (2) except that the A blocks represent 55 wt. '7: and the B block represents 45 wt. /r.

ABA block polymer; B block derived from polyethylene glycol 6000. A blocks represent 33 wt. /1 nxypentamethylencarbonyl units and B block represents 67 wt. "/1 oxyethylene units.

Same as footnote (6) except that A blocks represent 30 wt. 71 and the B block represents 70 wt. /r.

"" An opacity value of l is the most opaque; blend has no TiO,.

EXAMPLES 33-34 A blend of Nylon 6 and the cyclic ester polymer prepared in the manner set out in Example 23 were spun into multifilament yarns. Samples of carpet were woven 37 from such yarns. The results of soil tests were determined and compared with a control (no cyclic ester in the blend). The results are set out in Table XX] below.

38 tic organic polymer. said percentages being based on the total weight of thermoplastic polymer and cyclic ester polymer.

TABLE XXI EXAMPLE CYCLlC ESTER 20 MINUTE CYCLE AFTER VACUUM AFI'ER VACUUM CLEANING NO. POLYMER; wt 7( WITH 0.02 GRAM SOIL CLEANING AND SHAMPOOING 33 Control Heavy Soiling Slight Improvement Very Slight Soiling Remaining 34 Light Soiling do. Restored to Original Condition ABA block polymer prepared according to the procedure set out in Example 23 using polyethylene glycol 6000. A blocks represent 30 wt 71 oxypentamethylene units and 8 block represents 70 Wt 7: uxyethylene units.

What is claimed is:

l. A thermoplastic composition consisting essentially of a blend of about 1 to about 95 weight percent of a cyclic ester polymer having a reduced viscosity of about 0.1 to about and containing at least a major molar amount of recurring units l of the formula:

' lil lii wherein each R, individually, is selected from the class consisting of hydrogen, alkyl, halo, and alkoxy, A is the oxy group; x is an integer from l to 4; is an integer from 1 to 4; z is an integer of zero or one; with the provisos that (a) the sum of x+y+z is at least 4 and not greater than 7, and (b) the total number of R substituents which are substituents other than hydrogen does not exceed 3, and up to a minor molar amount of recurring units ll of the formula:

, thereof having 2 to l8 carbon atoms as the thermoplas- 2. Composition as claimed in claim 1 wherein said cyclic ester polymer consists essentially of units 1.

3. Composition as claimed in claim 1 wherein said cyclic ester polymer consists essentially of units 1 and ll.

4. Composition as claimed in claim 1 wherein said cyclic ester polymer is present in a minor weight amount and said thermoplastic organic polymer is present in a major weight amount.

5. Composition as claimed in claim I wherein said cyclic ester polymer is present in the amount of about 2 to about 40 percent and said thermoplastic organic polymer is present in the amount of about 60 to about 98 percent based on the total weight of cyclic ester polymer and thermoplastic organic polymer.

6. Composition as claimed in claim 1 wherein said cyclic ester polymer is present in the amount of about 5 to about 30 percent and said thermoplastic organic polymer is present in the amount of about to about percent based on the total weight of cyclic ester polymer and thermoplastic organic polymer.

7. Composition as claimed in claim 1 wherein said cyclic ester polymer is characterized by the recurring structural recurring unit: 

1. A THERMOPLASTIC COMPOSITION CONSISTING ESSENTIALLY OF A BLEND OF ABOUT 1 TO ABOUT 95 WEIGHT PERCENT OF A CYCLIC ESTER POLYMER HAVING A REDUCED VISCOSITY OF ABOUT 0.1 TO ABOUT 15 AND CONTAINING AT LEAST A MAJOR MOLAR AMOUNT OF RECURRING UNITS 1 OF THE FORMULA:
 2. Composition as claimed in claim 1 wherein said cyclic ester polymer consists essentially of units I.
 3. Composition as claimed in claim 1 wherein said cyclic ester polymer consists essentially of units I and II.
 4. Composition as claimed in claim 1 wherein said cyclic ester polymer is present in a minor weight amount and said thermoplastic organic polymer is present in a major weight amount.
 5. Composition as claimed in claim 1 wherein said cyclic ester polymer is present in the amount of about 2 to about 40 percent and said thermoplastic organic polymer is present in the amount of about 60 to about 98 percent based on the total weight of cyclic ester polymer and thermoplastic organic polymer.
 6. Composition as claimed in claim 1 wherein said cyclic ester polymer is present in the amount of about 5 to about 30 percent and said thermoplastic organic polymer is present in the amount of about 70 to about 95 percent based on the total weight of cyclic ester polymer and thermoplastic organic polymer.
 7. Composition as claimed in claim 1 wherein said cyclic ester polymer is characterized by the recurring structural recurring unit:
 8. Composition as claimed in claim 1 wherein said thermoplastic polymer is poly(ethylene terephthalate). 